CN1714160A - Method for making an abrasion resistant steel plate and plate obtained - Google Patents

Method for making an abrasion resistant steel plate and plate obtained Download PDF

Info

Publication number
CN1714160A
CN1714160A CNA2003801036477A CN200380103647A CN1714160A CN 1714160 A CN1714160 A CN 1714160A CN A2003801036477 A CNA2003801036477 A CN A2003801036477A CN 200380103647 A CN200380103647 A CN 200380103647A CN 1714160 A CN1714160 A CN 1714160A
Authority
CN
China
Prior art keywords
workpiece
arbitrary described
sheet material
steel
content
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
CNA2003801036477A
Other languages
Chinese (zh)
Other versions
CN100350061C (en
Inventor
让·贝吉诺
让-乔治·布里松
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Industeel France SAS
Original Assignee
Industeel Creusot
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Industeel Creusot filed Critical Industeel Creusot
Publication of CN1714160A publication Critical patent/CN1714160A/en
Application granted granted Critical
Publication of CN100350061C publication Critical patent/CN100350061C/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

The invention concerns a method for making an abrasion resistant steel plate having a chemical composition comprising: 0.35 % </= C </= 0.8 %, 0 % </= Si </= 2 %; 0 % </= AI </= 2 %; 0.35 % </= Si + AI </= 2 %; 0 % </= Mn </= 2.5 %; 0 % </= Ni </= 5 %; 0 % </= Cr </= 5 %; 0 % </= Mo </= 0.050; 0 % </= W </= 1 %; 0,1 % </= Mo +W/2 </= 0.5 %; 0 % </= B </= 0.02 %; 0 % </= Ti </= 2 %; 0 % </= Zr </= 4 %; 0.05 % </= Ti + Zr/2 </= 2 %; 0 % </= S </= 0.15 %; N </= 0,03; optionally 0 % to 1.5 % of Cu; optionally Nb, Ta or V with Nb/2 + Ta/4 + V </= 0.5 %; optionally less than 0.1 % of Se, Te, Ca, Bi or Pb; the rest being iron and impurities; the composition satisfying: 0.1 % < C* = C - Ti/4 - Zr/8 + 7xN/8 </= 0.55 % and 1.05xMn + 0.54xNi +0.5OxCr + 0.3x(Mo + W/2)<1/2> + K > 1.8, with K = 0.5 if B >/= 0.0005 % and K = 0 if B < 0.0005 % and Ti+Zr/2-7xN/2 >/= 0.05 %; hardening after austenitization while cooling at a speed > 0,5 DEG C/s between a temperature > AC3 and ranging between T = 800 - 270xC* - 9OxMn -37xNi - 70XCr - 83x(Mo + W/2) and T-50 DEG C; then at a core speed Vr < 1150XEP<-1.7> between T and 100 DEG C, (ep = plate thickness in mm); cooling down to room temperature. The invention also concerns the resulting plate.

Description

Prepare the method for wear-resisting steel plate and the steel plate that makes thus
Technical field
The present invention relates to wear-resisting steel and preparation method thereof.
Background technology
Known wear-resisting steel have high hardness (400 to 500Brinell) usually, have martensitic structure and contain 0.12% to 0.3% carbon.It has been generally acknowledged that,, need only improve the hardness of steel, but can destroy other characteristic of steel, for example welding characteristic or bending forming characteristic like this in order to improve wear resistance.Therefore, in order to obtain the steel that not only have extraordinary wear resistance but also have favorable applicability, people begin to attempt other method except that increasing hardness.
In order to improve the wear resistance of steel, EP 0527276 and US 5,393,0.015% to 1.5% titanium is added in 358 suggestions in steel, to form thick titanium carbide, contain 0.05% to 0.45% carbon in the described steel, be not higher than 1% silicon, be not higher than 2% manganese, be not higher than 2% copper, be not higher than 10% nickel, be not higher than 3% chromium and be not higher than 3% molybdenum, boron, niobium and vanadium.Described steel are quenched so that it has martensitic structure, and the appearance of thick titanium carbide makes the wear resistance of steel be improved.Yet when described steel was cast stick, the improvement of described wear resistance was restricted, because under the effect of wearing and tearing stress (abrasive stress), carbide can be separated, thereby can't play a role.And the existence of thick titanium carbide has influenced the ductility of steel in these steel.Therefore, the steel plate that is got by described steel is difficult to finish rolling and bending, thereby has limited their application.
Summary of the invention
The objective of the invention is and will overcome the above-mentioned defective of prior art by a kind of attrition resistant steel plate is provided, described steel plate has the surface of good planeness, and is keeping under the constant situation of other characteristic, and the wear resistance of described steel plate is better than known steel.
For this reason, the present invention relates to a kind of particularly method of sheet material of attrition resistant steel workpiece for preparing, the chemical constitution of described workpiece comprises by weight:
0.35％≤C≤0.8％；
0％≤Si≤2％；
0％≤Al≤2％；
0.35％≤Si+Al≤2％；
0％≤Mn≤2.5％；
0％≤Ni≤5％；
0％≤Cr≤5％；
0％≤Mo≤0.050％；
0％≤W≤1.00％；
0.1％≤Mo+W/2≤0.50％；
0％≤Cu≤1.5％；
0％≤B≤0.02％；
0％≤Ti≤2％；
0％≤Zr≤4％；
0.05％≤Ti+Zr/2≤2％；
0％≤S≤0.15％；
N＜0.03％；
-optional at least a the element that is selected from Nb, Ta and V, their content satisfies Nb/2+Ta/4+V≤0.5%;
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, its content is less than or equals 0.1%;
The impurity that produces in the iron of-surplus and the preparation process;
Described chemical constitution also satisfies following relation:
0.10%≤C *≤ 0.55%, C wherein *=C-Ti/4-Zr/8+7 * N/8 and
Ti+Zr/2-7 * N/2 〉=0.05% and
1.05 * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2) 1/2+ K＞1.8, more preferably greater than 2, wherein, if B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0;
According to described method, in the thermoforming heat of for example rolling heat, described workpiece or sheet material are carried out the hot quenching processing, perhaps after austenitizing, implement quench treatment by reheat in stove, described quench treatment comprises:
-cool off described workpiece or sheet material with average rate of cooling greater than 0.5 ℃/s, with temperature from being higher than AC 3Temperature reduce to T=800-270 * C *-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2) and between T-50 ℃, wherein temperature is with a ℃ expression, C *, Mn, Cr, Mo and W content represent with weight %;
-subsequently with less than 1150 * ep -1.7(in ℃/s) and average core rate of cooling (the core cooling rate) Vr that is higher than 0.1 ℃/s cool off described workpiece or sheet material, temperature is reduced to 100 ℃ from T, wherein ep is the thickness of slab in mm;
-then described workpiece or sheet material are cooled to room temperature, and choose wantonly and carry out finish rolling processing (planishing).
After quenching, choose wantonly and carry out temper under the temperature that is being lower than 350 ℃, and preferably carry out temper being lower than under 250 ℃ the temperature.
The invention still further relates to a kind of workpiece that is made by aforesaid method, particularly sheet material, described steel comprise 5% to 20% retained austenite, and surplus is martensitic structure or martensite/bainite structure and carbide.When described workpiece was sheet material, its thickness can be 2mm to 150mm, and its surface finish is shown with deviation card and is less than or equal to 12mm/m, preferably less than 5mm/m.
When carbon content satisfied 0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.2%, steel hardness was between 280HB to 450HB.
When carbon content satisfied 0.2%＜C-Ti/4-Zr/8+7 * N/8≤0.3%, steel hardness was between 380HB to 550HB.
When carbon content satisfied 0.3%＜C-Ti/4-Zr/8+7 * N/8≤0.5%, steel hardness was between 450HB to 650HB.
Describe the present invention in detail below by embodiment, but these are not limitation of the present invention.
In order to prepare sheet material of the present invention, the steel that preparation has following chemical constitution in weight %:
-0.35% to 0.8% carbon, preferred carbon content are higher than 0.45% or be higher than 0.5%; 0% to 2% Ti, 0% to 4% Zr, the content of Ti and Zr satisfies 0.05%≤Ti+Zr/2≤2%.Carbon is mainly used in and forms sufficiently rigid martensitic structure, and is used to form the carbide of Ti and/or Zr.The total amount of Ti+Zr/2 must be higher than 0.05%, preferably be higher than 0.10%, more preferably be higher than 0.3%, more preferably be higher than 0.5% again, draw the minimum of formed carbide thus, but it must be lower than 2%, preferably smaller or equal to 0.9%, because be higher than this level, the toughness of steel and suitability can be affected.
The Al of the Si and 0% (or trace) of-0% (or trace) to 2% to 2%, the total amount of Si+Al is preferably greater than 0.5%, more preferably greater than 0.7% between 0.35% to 2%.These elements are not only reductor, also have the effect of the formation that promotes metastable retained austenite, and described austenite contains a large amount of carbon, and it follows bigger expansion when changing into martensitic structure, and this can promote the set of titanium carbide.
The Cr of the Mn of-0% (or trace) to 2% or 2.5%, 0% (or trace) Ni and 0% (or trace) to 4% or 5% to 4% or 5% is so that obtain enough quenchability (quenchability) and adjust various mechanical characteristics or use properties.Nickel is for raising toughness particularly advantageous, but nickel is comparatively expensive.Chromium also can form thin carbide in martensite or bainite structure.
The Mo of-0% (or trace) to 0.50%.This element can improve quenchability and form thin sclerosis carbide in martensite or bainite structure, particularly by the deposition that causes owing to auto-tempering in process of cooling.The content of Mo need not to surpass 0.50% can reach the ideal effect, particularly for the deposition of sclerosis carbide.Can use the tungsten of twice consumption partly or entirely to replace molybdenum.Yet in fact this replacement is unfavorable, does not bring more benefit and price more expensive because compare tungsten with molybdenum.
-optional 0% to 1.5% copper.Copper can bring additional hardening effect under the situation that does not influence weldability.Copper content is higher than at 1.5% o'clock, and effect does not significantly improve, and causes hot rolling difficulty and unnecessary cost to increase on the contrary.
-0% to 0.02% B.The optional boron that adds improves quenchability.In order to reach required effect, the content of boron preferably is higher than 0.0005%, more preferably is higher than 0.001%, but need not basically to surpass 0.01%.
-be no more than 0.15% sulphur.As resistates, the content of element sulphur is limited in 0.005% or lower usually, but in order to improve workability, also can initiatively carry doctor positive content.Should be pointed out that to exist under the situation of sulphur that for fear of encountering difficulties, the content of manganese must be higher than 7 times of sulphur content in thermal distortion.
-optional at least a the element that is selected among Nb, Ta and the V, their content satisfies Nb/2+Ta/4+V≤0.5%, so that form thicker carbide, thereby improves wear resistance.But the effect of the carbide that is formed by these elements is effective not as the carbide that formed by titanium or zirconium, therefore, and optional these elements of interpolation, and limit their consumption.
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, wherein every kind of content all is less than 0.1%.These elements are used to improve workability.Should be pointed out that when containing Se and/or Te in the steel, consider the content of sulphur, the content of manganese will guarantee to form the selenide or the telluride of manganese.
The impurity that produces in the iron of-surplus and the preparation process.Described impurity especially comprises nitrogen, and nitrogen content depends on the preparation method, but is no more than 0.03% usually.The nitrogen element can form nitride in titanium or zirconium reaction, and formed nitride necessarily can not be too thick, in order to avoid infringement toughness.In order to prevent to form thick nitride; can in molten steel, add titanium and zirconium very lentamente; for example oxidation phase (slag that for example contains the oxide compound of titanium or zirconium) can be contacted with the oxidation molten steel, then with deoxidation of molten steel, so that titanium or zirconium slowly are diffused into the molten steel mutually from oxidation.
In addition, in order to obtain satisfied characteristic, the content of carbon, titanium, zirconium and nitrogen element must satisfy: 0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.55%,
C-Ti/4-Zr/8+7 * N/8=C wherein *, C *Be illustrated in the carbide free carbon content afterwards of titanium deposition and zirconium, consider the formation of the nitride of titanium and zirconium.Described free carbon content must be higher than 0.1%, and is preferably greater than or equals 0.22% so that martensite has minimum hardness, but free carbon content be higher than at 0.55% o'clock can grievous injury toughness and suitability.
Consider the thickness of the sheet material that will produce, must further select to have enough quenchability to guarantee steel to above-mentioned chemical constitution.For this reason, described chemical constitution also must satisfy following relation:
Quench index (Quench)=1.05 * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2) 1/2+ K＞1.8 are preferably greater than 2, if wherein B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0.
Should be pointed out that in order to promote the formation of retained austenite when quench index was between 1.8 and 2.0, the content of preferred silicon was higher than 0.5%.
In addition, in order to guarantee the enough content of carbide, the content of Ti, Zr and N preferably satisfies: Ti+Zr/2-7 * N/2 〉=0.05%, and more preferably greater than 0.1%, again more preferably greater than 0.3%.
At last, in order to obtain good wear resistance, the microtexture of described steel mainly is made of the mixed structure of martensite or bainite structure or two kinds of structures, and comprises 5% to 20% austenitic structure; Described structure also comprises thick titanium or zirconium carbide or niobium, tantalum or the vanadium carbide that at high temperature forms.The inventor finds that separating out too early of described thick carbide can the thick carbide of infringement improve the effect of wear resistance, metastable austenitic existence then can prevent separating out too early of carbide, because these austenites that influence of wear phenomenon are converted to new martensite.Because metastable austenite often is accompanied by expansion to new martensitic conversion, the described conversion that occurs in the wearing and tearing subgrades (abraded sub-layer) helps stoping separating out of carbide, thereby improves wearing and tearing patience.
In addition, because the hardness of described steel is higher and wherein also have the titanium carbide of embrittlement, need reduce the finish rolling operation as much as possible.Given this, the inventor finds the rate of temperature fall by fully slowing down between the bainite/martensite zone of transformation, can reduce the residual set of product, thereby can reduce the finish rolling operation.The inventor finds by with less than 1150 * ep -1.7(wherein ep is in the thickness of slab of mm, rate of cooling with ℃/s represents) rate of cooling Vr cool the temperature to and be lower than T=800-270 * C *-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2), (with a ℃ expression) promoted the generation of the residual austenite of remarkable ratio on the one hand, also reduced the unrelieved stress that is caused by phase transformation on the other hand.
In order to prepare very flat sheet material, prepare described steel and it is cast into sheet material or bar with good wear resistance.Described sheet material or rod hot rolling with preparation sheet material, are heat-treated this sheet material then, so that without further finish rolling or the structure and the surface of good planeness that obtain to wish by limited finish rolling.Described thermal treatment can directly be pined for carrying out also can carrying out subsequently in rolling, chooses wantonly after cold finish rolling or middle temperature finish rolling.
In order to carry out described heat treatment operation:
-described steel are heated above AC 3Point is so that convert it into austenitic structure completely;
-then,, be cooled to and be equal to or slightly less than temperature T (than low about 50 ℃ of T), described temperature T=800-270 * C its average rate of cooling with the critical conversion rate that is higher than bainite *-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2), (with a ℃ expression);
-subsequently, with less than 1150 * ep -1.7(to obtain desirable structure) and the average core rate of cooling Vr that is higher than 0.1 ℃/s (to obtain enough hardness) cool off described sheet material, and temperature is reduced to about 100 ℃ from said temperature (promptly about T to than T-50 ℃ between);
-then described sheet material is cooled to room temperature, preferred low rate of cooling but and nonessential.
In addition, can be less than or equal under 350 ℃ the temperature, preferably, carry out stress relief and handle being less than or equal under 250 ℃ the temperature.
Can make a kind of sheet material by this way, its thickness can be between 2mm to 150mm, and without finish rolling or only through it has excellent surface finish under the situation of appropriate finish rolling, described surface finish is expressed as less than 12mm/m with deviation (deflection).The hardness of described sheet material is between 280HB to 650HB.This hardness depends on the content C of free carbon basically *=C-Ti/4-Zr/8+7 * N/8.
Along with free carbon content C *Increase, the firmness level raises, particularly:
If a) 0.1%≤C *≤ 0.2%, then hardness is greatly about between the 280HB to 450HB;
B) if 0.2%＜C *≤ 0.3%, then hardness is greatly about between the 380HB to 550HB;
C) if 0.3%＜C *≤ 0.5%, then hardness is greatly about between the 450HB to 650HB.
Because hardness is free carbon content C *Function, can adopt different titaniums or zirconium content to obtain identical hardness.Under the identical situation of hardness, along with the increase of the content of titanium or zirconium, wear resistance gets a promotion.Similarly, when the content of titanium or zirconium is identical, along with the increase wear resistance of hardness also improves.In addition, along with the minimizing of free carbon content, the use of described steel becomes easier, but for identical free carbon content, the ductility of steel improves along with the minimizing of titanium content.By considering above-mentioned factor, can select carbon content and titanium or zirconium content to make the steel that are fit to each Application Areas.
According to the difference of hardness, steel for example can be used for following purposes:
-between 280HB to 450HB: the tank car of shovel, truck or dump car, hurricane shielding, hopper and concrete mold;
-between 380HB to 550HB: the scraper plate and the screen cloth grid of the shield of bump shredder, blade, clamshell-type dump bucket;
-between 450HB to 650HB: the reinforcing member under the shielding slab of cartridge type shredder, the reinforcing member of hopper, the primary blades, cut wiper blade shielding (cut-water blade shields), major cutting edge (leading edges).
For instance, investigate according to steel plate A to G of the present invention and prior art steel plate H to J.The chemical constitution of steel plate is (with 10 -3Weight % represents), the content and the abrasion resistance index Rus of hardness, retained austenite structure list in the table 1.
Table 1
??C ??Si ??Al ??Mn ??Ni ??Cr ??Mo ??W ??Ti ??B ??N ??HB The % austenite ??Rus
??A ??360 ??850 ??50 ??1300 ??500 ??700 ??100 ??500 ??400 ??2 ??6 ??460 ??10 ??1.42
??B ??640 ??850 ??50 ??400 ??1500 ??700 ??110 ??450 ??620 ??3 ??7 ??555 ??14 ??2.72
??C ??590 ??520 ??570 ??550 ??320 ??1850 ??470 ??- ??540 ??- ??7 ??570 ??12 ??2.24
??D ??705 ??460 ??630 ??1090 ??280 ??2450 ??430 ??100 ??825 ??- ??7 ??580 ??13 ??3.14
??E ??690 ??370 ??25 ??740 ??310 ??2100 ??460 ??- ??795 ??- ??6 ??605 ??10 ??2.83
??F ??350 ??810 ??30 ??1200 ??270 ??1350 ??380 ??160 ??2 ??6 ??510 ??8 ??1.32
??G ??390 ??790 ??35 ??1210 ??250 ??1340 ??390 ??405 ??3 ??6 ??495 ??11 ??1.77
??H ??340 ??380 ??30 ??1260 ??470 ??820 ??370 ??- ??410 ??3 ??6 ??475 ??1 ??0.86
??I ??315 ??330 ??25 ??1230 ??180 ??1360 ??395 ??165 ??2 ??6 ??515 ??2 ??0.7
??J ??367 ??315 ??30 ??1215 ??210 ??1375 ??405 ??430 ??2 ??5 ??500 ??2 ??1.01
Rotation prism-shaped sample in the container that the graded quartz pellet is housed, abrasion resistance index Rus changes with the variation of the antilogarithm of the weight loss of this sample.
The thickness of these sheet materials is 30mm, and the sheet material corresponding to steel A to G is quenched after 900 ℃ are carried out austenitizing according to the present invention.
After austenitizing, cooling conditions is as follows:
-for the sheet material of making by steel B and D: according to the inventive method, cool the temperature on the said temperature T with the average rate of cooling of 0.7 ℃/s, the average rate of cooling with 0.13 ℃/s cools the temperature under the T then;
-for the sheet material of making by steel A, C, E, F and G: according to the inventive method, cool the temperature on the said temperature T with the average rate of cooling of 6 ℃/s, the average rate of cooling with 1.4 ℃/s cools the temperature under the T then;
-in contrast the sheet material of making by steel H, I and J: carry out austenitizing at 900 ℃, then the average rate of cooling with 20 ℃/s cools the temperature on the said temperature T, and the average rate of cooling with 12 ℃/s cools the temperature under the T then.
Sheet material according to the present invention has martensite/bainite structure, wherein contains 5% to 20% retained austenite, and contrast sheet material then has martensitic structure completely, that is to say that contained retained austenite is no more than 2 to 3% martensitic structure.These sheet materials all contain carbide.
To comparison shows that of wear resistance, under similar hardness and titanium content, the abrasion resistance index Rus of sheet material of the present invention on average exceeds 0.5 than the abrasion resistance index Rus of prior art sheet material.Especially, the contrast table of diverse embodiment A of structure and H (content of retained austenite is 10% among the A, then all is martensite among the H) is understood the probability that occurs retained austenite in the structure.The difference that should be pointed out that retained austenite content is because the difference of heat treatment operation is because the difference of silicone content on the other hand on the one hand.
Find also that in addition under the identical situation of other factors, and the situation of carbonaceous deposits in the matrix that does not contain retained austenite compared, the coexistence of titanium carbide and retained austenite among the present invention causes titanium carbide obviously higher to the contribution of wear resistance.Therefore, therefore identical titanium content difference (identical TiC content difference, carbon is still excessive) caused wear resistance increase in F steel and G steel (steel of the present invention) is different from obviously that caused wear resistance increases in I steel and J steel.For F steel and G steel, increase to 0.46 by the caused abrasion resistance index Rus of 0.245% Ti, and for I steel and J steel, being increased by the caused abrasion resistance index Rus of 0.265% Ti only is 0.31.
Above-mentioned phenomenon can be owing to the improve of matrix around when containing retained austenite in the matrix to the jam-packed effect (squeezing effect) of titanium carbide, these retained austenites can change into hard martensitic structure under the effect of wearing and tearing stress, and described conversion process is accompanied by bigger expansion.
In addition, less than 10mm/m, and be 15mm/m without the cooling after strain of the steel plate of the present invention of finish rolling for the described cooling after strain of H steel plate.
In actual applications, can can provide product without finish rolling according to the present invention, perhaps carry out finish rolling, but described finish rolling is more or less freely and only need use less pressure, because the distortion of product of the present invention itself is less in order to satisfy stricter surface finish to require (for example 5mm/m).

Claims (20)

1, a kind of method for preparing attrition resistant steel workpiece such as sheet material, the chemical constitution of described workpiece comprises by weight:
0.35％≤C≤0.8％；
0％≤Si≤2％；
0％≤Al≤2％；
0.35％≤Si+Al≤2％；
0％≤Mn≤2.5％；
0％≤Ni≤5％；
0％≤Cr≤5％；
0％≤Mo≤0.50％；
0％≤W≤1.00％；
0.1％≤Mo+W/2≤0.50％；
0％≤B≤0.02％；
0％≤Ti≤2％；
0％≤Zr≤4％；
0.05％≤Ti+Zr/2≤2％；
0％≤S≤0.15％；
N＜0.03％；
-optional 0% to 1.5% copper;
-optional at least a the element that is selected among Nb, Ta and the V, their content satisfies Nb/2+Ta/4+V≤0.5%;
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, its content is less than or equals 0.1%;
The impurity that produces in the iron of-surplus and the preparation process;
Described chemical constitution also satisfies following relation:
0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.55% and
Ti+Zr/2-7 * N/2 〉=0.05% and
1.05 1/2+K＞1.8 of * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2), wherein, if B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0;
According to described method, in the thermoforming heat of for example rolling heat, described sheet material is carried out hot quenching and handle, perhaps after austenitizing, implement quench treatment by reheat in stove, described quench treatment comprises:
-cool off described workpiece or sheet material with average rate of cooling greater than 0.5 ℃/s, with temperature from being higher than AC 3Temperature reduce to T=800-270 * C *-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2) and between T-50 ℃, wherein C *=C-Ti/4-Zr/8+7 * N/8;
-subsequently with less than 1150 * ep -1.7And the average core rate of cooling Vr that is higher than 0.1 ℃/s cools off described workpiece or sheet material, and temperature is reduced to 100 ℃ from T, and wherein ep is the thickness of slab in mm;
-then described workpiece or sheet material are cooled to room temperature, and choose wantonly and carry out the finish rolling processing.
2, according to the method for claim 1, it is characterized in that:
1.05×Mn+0.54×Ni+0.50×Cr+0.3×(Mo+W/2) 1/2+K＞2。
3, according to the method for claim 1 or 2, it is characterized in that: C＞0.45%.
4, according to the arbitrary described method of claim 1-3, it is characterized in that:
Si+Al＞0.5％。
5, according to the arbitrary described method of claim 1-4, it is characterized in that:
Ti+Zr/2＞0.10％。
6, according to the arbitrary described method of claim 1-5, it is characterized in that:
Ti+Zr/2＞0.30％。
7, according to the arbitrary described method of claim 1-6, it is characterized in that:
C *≥0.22％。
8,, it is characterized in that again carrying out temper being less than or equal under 350 ℃ the temperature according to the arbitrary described method of claim 1-7.
9,, it is characterized in that molten steel being contacted with the titaniferous slag, so that the titanium in the slag slowly is diffused in the molten steel in order in steel, to add titanium according to the arbitrary described method of claim 1-8.
10, a kind of attrition resistant steel workpiece such as sheet material, the chemical constitution of described workpiece comprises by weight:
0.35％≤C≤0.8％；
0％≤Si≤2％；
0％≤Al≤2％；
0.35％≤Si+Al≤2％；
0％≤Mn≤2.5％；
0％≤Ni≤5％；
0％≤Cr≤5％；
0％≤Mo≤0.50％；
0％≤W≤1.00％；
0.1％≤Mo+W/2≤0.50％；
0％≤B≤0.02％；
0％≤Ti≤2％；
0％≤Zr≤4％；
0.05％≤Ti+Zr/2≤2％；
0％≤S≤0.15％；
N＜0.03％；
-optional 0% to 1.5% copper;
-optional at least a the element that is selected among Nb, Ta and the V, their content satisfies Nb/2+Ta/4+V≤0.5%;
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, its content is less than or equals 0.1%;
The impurity that produces in the iron of-surplus and the preparation process;
Described chemical constitution also satisfies following relation:
0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.55% and
Ti+Zr/2-7 * N/2 〉=0.05% and
1.05 * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2) 1/2+ K＞1.8, wherein, if B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0;
Its surface finish is shown less than 12mm/m with deviation card, and described steel have martensitic structure or martensite/bainite structure, also comprises 5% to 20% retained austenite and carbide in the described structure.
11, according to the workpiece of claim 10, it is characterized in that:
1.05×Mn+0.54×Ni+0.50×Cr+0.3×(Mo+W/2) 1/2+K＞2。
12, according to the workpiece of claim 10 or 11, it is characterized in that: C＞0.45%.
13, according to the arbitrary described workpiece of claim 10-12, it is characterized in that:
Si+Al＞0.5％。
14, according to the arbitrary described workpiece of claim 10-13, it is characterized in that:
Ti+Zr/2＞0.10％。
15, according to the arbitrary described workpiece of claim 10-14, it is characterized in that:
Ti+Zr/2＞0.30％。
16, according to the arbitrary described workpiece of claim 10-15, it is characterized in that:
C *≥0.22％。
17,, it is characterized in that it is that thickness is the sheet material of 2mm to 150mm, and its surface finish is shown less than 12mm/m with deviation card according to the arbitrary described workpiece of claim 10-16.
18, according to the arbitrary described workpiece of claim 10-17, it is characterized in that its hardness between 280HB to 450HB, and 0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.2%.
19, according to the arbitrary described workpiece of claim 10-17, it is characterized in that its hardness between 380HB to 550HB, and 0.2%＜C-Ti/4-Zr/8+7 * N/8≤0.3%.
20, according to the arbitrary described workpiece of claim 10-17, it is characterized in that its hardness between 450HB to 650HB, and 0.3%＜C-Ti/4-Zr/8+7 * N/8≤0.5%.
CNB2003801036477A 2002-11-19 2003-11-13 Method for making an abrasion resistant steel plate and plate obtained Expired - Lifetime CN100350061C (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR02/14424 2002-11-19
FR0214424A FR2847270B1 (en) 2002-11-19 2002-11-19 METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET

Publications (2)

Publication Number Publication Date
CN1714160A true CN1714160A (en) 2005-12-28
CN100350061C CN100350061C (en) 2007-11-21

Family

ID=32187695

Family Applications (1)

Application Number Title Priority Date Filing Date
CNB2003801036477A Expired - Lifetime CN100350061C (en) 2002-11-19 2003-11-13 Method for making an abrasion resistant steel plate and plate obtained

Country Status (20)

Country Link
US (3) US7459041B2 (en)
EP (1) EP1563104B1 (en)
JP (1) JP4535877B2 (en)
KR (1) KR101010570B1 (en)
CN (1) CN100350061C (en)
AR (1) AR042071A1 (en)
AT (1) ATE400667T1 (en)
AU (1) AU2003290188B2 (en)
BR (2) BR0315697B1 (en)
CA (1) CA2506351C (en)
DE (1) DE60322092D1 (en)
ES (1) ES2309377T3 (en)
FR (1) FR2847270B1 (en)
PE (1) PE20040487A1 (en)
PL (1) PL204080B1 (en)
RU (1) RU2327802C2 (en)
SI (1) SI1563104T1 (en)
UA (1) UA80308C2 (en)
WO (1) WO2004048620A1 (en)
ZA (1) ZA200504005B (en)

Cited By (30)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102199737A (en) * 2010-03-26 2011-09-28 宝山钢铁股份有限公司 600HB-grade wear resistant steel plate and its manufacturing method
CN101775545B (en) * 2009-01-14 2011-10-12 宝山钢铁股份有限公司 Low-alloy high-strength high-toughness wear-resistant steel plate and manufacturing method thereof
CN102433505A (en) * 2011-12-14 2012-05-02 虞海盈 Material for producing rolling bearings
CN102453791A (en) * 2010-10-15 2012-05-16 本特勒尔汽车技术有限公司 Automobile column and method for producing a hot-formed and press-hardened automobile column
CN102134682B (en) * 2010-01-22 2013-01-02 宝山钢铁股份有限公司 Wear resistant steel plate
CN103205639A (en) * 2013-03-14 2013-07-17 长安大学 Shovel blade cutting edge of loader and method for manufacturing shovel blade cutting edge
CN103320695A (en) * 2013-06-19 2013-09-25 侯宇岷 Large-diameter wear-resistant steel ball and production process thereof
CN103748288A (en) * 2011-08-20 2014-04-23 卡特彼勒公司 Bimaterial flight assembly for an elevator system for a wheel tractor scraper
CN103898299A (en) * 2014-04-04 2014-07-02 北京科技大学 Preparation method for 2400MPa class low-cost nano bainitic steel
CN103958718A (en) * 2011-11-01 2014-07-30 霍尼韦尔国际公司 Low nickel austenitic stainless steel
CN104032216A (en) * 2014-06-27 2014-09-10 张家港市佳威机械有限公司 Composite manganese-steel alloy
CN104131224A (en) * 2014-07-25 2014-11-05 合肥市东庐机械制造有限公司 Wear-resistant impact-resistant alloy steel and manufacturing method thereof
CN104152820A (en) * 2014-07-16 2014-11-19 安徽省三方耐磨股份有限公司 Novel alloy lining plate
CN104213041A (en) * 2014-08-28 2014-12-17 南京赛达机械制造有限公司 Wear-resisting steel for turbine blade and production process t hereof
CN105018863A (en) * 2015-07-13 2015-11-04 江苏曜曜铸业有限公司 Alloy used for clutch housing mould
CN105039864A (en) * 2015-07-13 2015-11-11 江苏曜曜铸业有限公司 Alloy used for spindle box mould
CN105506481A (en) * 2014-09-29 2016-04-20 铜陵有色金神耐磨材料有限责任公司 Manufacturing method of impact-resistant alloy grinding balls
CN105568142A (en) * 2016-03-09 2016-05-11 桂林电子科技大学 High-strength and high-tenacity low-alloy wear-resistant steel excavator bucket tooth and preparing method thereof
CN105723004A (en) * 2013-08-30 2016-06-29 罗奇钢铁公司 A high-hardness hot-rolled steel product, and a method of manufacturing the same
CN105779891A (en) * 2016-04-15 2016-07-20 芜湖德业摩擦材料有限公司 Preparation method for high-hardness friction block for brake pad
CN105886946A (en) * 2016-04-15 2016-08-24 芜湖德业摩擦材料有限公司 Preparing method of brake pad friction block
CN106811680A (en) * 2016-12-28 2017-06-09 芜湖市永帆精密模具科技有限公司 A kind of low-alloy impact-resistant abrasion-proof steel ball and preparation method thereof
US9689050B2 (en) 2011-09-06 2017-06-27 Arcelormittal Investigación Y Desarrollo S.L. Rolled steel that hardens by means of precipitation after hot-forming and/or quenching with a tool having very high strength and ductility, and method for manufacturing same
CN111647820A (en) * 2020-06-15 2020-09-11 山东建筑大学 Advanced high-strength steel and segmented preparation method and application thereof
CN111690880A (en) * 2020-08-08 2020-09-22 湖南长重机器股份有限公司 Impact-resistant lining plate of bucket wheel machine hopper
CN112695253A (en) * 2020-12-22 2021-04-23 江西耐普矿机股份有限公司 Carbide-containing high-strength high-toughness bainite wear-resistant steel and preparation method thereof
CN112703263A (en) * 2018-09-12 2021-04-23 杰富意钢铁株式会社 Steel material and method for producing same
CN112899571A (en) * 2021-01-19 2021-06-04 山东钢铁股份有限公司 Fatigue-resistant corrosion-resistant round steel for forging and pressing and preparation method thereof
CN113444985A (en) * 2021-05-24 2021-09-28 北京中永业科技有限公司 Steel material and preparation method thereof
CN114729435A (en) * 2019-12-16 2022-07-08 株式会社Posco High-hardness wear-resistant steel with excellent low-temperature impact toughness and manufacturing method thereof

Families Citing this family (28)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2847274B1 (en) * 2002-11-19 2005-08-19 Usinor SOLDERABLE CONSTRUCTION STEEL PIECE AND METHOD OF MANUFACTURE
FR2847272B1 (en) * 2002-11-19 2004-12-24 Usinor METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET
US8669491B2 (en) 2006-02-16 2014-03-11 Ravi Menon Hard-facing alloys having improved crack resistance
JP4894297B2 (en) * 2006-02-28 2012-03-14 Ｊｆｅスチール株式会社 Wear-resistant steel plate
JP4894296B2 (en) * 2006-02-28 2012-03-14 Ｊｆｅスチール株式会社 Wear-resistant steel plate
US20080073006A1 (en) * 2006-09-27 2008-03-27 Henn Eric D Low alloy steel plastic injection mold base plate, method of manufacture and use thereof
US8137483B2 (en) * 2008-05-20 2012-03-20 Fedchun Vladimir A Method of making a low cost, high strength, high toughness, martensitic steel
DE102010050499B3 (en) * 2010-11-08 2012-01-19 Benteler Automobiltechnik Gmbh Use of a wear-resistant steel component
RU2458177C1 (en) * 2010-12-03 2012-08-10 Открытое акционерное общество "Магнитогорский металлургический комбинат" Strip rolled products from boron-containing manganese steel
CN103620075B (en) * 2011-06-10 2016-02-17 株式会社神户制钢所 Hot compacting product, its manufacture method and hot compacting steel sheet
CN102560272B (en) * 2011-11-25 2014-01-22 宝山钢铁股份有限公司 Ultrahigh-strength abrasion-resistant steel plate and manufacturing method thereof
ES2744909T3 (en) 2013-06-07 2020-02-26 Nippon Steel Corp Heat treated steel material and method of manufacture thereof
US20150037198A1 (en) * 2013-07-30 2015-02-05 Caterpillar Inc. Wear resistant high toughness steel
CN103757552B (en) * 2013-12-17 2016-01-20 界首市华盛塑料机械有限公司 A kind of cutting tool alloy steel material and preparation method thereof
RU2546262C1 (en) * 2014-01-09 2015-04-10 Публичное акционерное общество "Северсталь" (ПАО "Северсталь") Wear-resistant steel and item made from it
CN104099534B (en) * 2014-08-01 2016-08-17 宁国市南方耐磨材料有限公司 A kind of ball mill abrasion-proof steel ball
CN104152808B (en) * 2014-08-24 2017-02-15 长兴德田工程机械股份有限公司 Boron-containing high-silicon bainite wear-resistant corrosion-resistant alloy and manufacturing method thereof
RU2557860C1 (en) * 2014-09-15 2015-07-27 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Южно-Уральский государственный университет" (национальный исследовательский университет) (ФГБОУ ВПО "ЮУрГУ" (НИУ)) Easy-to-machine structural chromium-manganese-molybdenum steel
RU2556189C1 (en) * 2014-09-15 2015-07-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Южно-Уральский государственный университет" (национальный исследовательский университет) (ФГБОУ ВПО "ЮУрГУ" (НИУ)) Easy treated structural medium carbon chrome-manganese-nickel-molybdenum steel
DE102014017273A1 (en) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh High strength air hardening multiphase steel with excellent processing properties and method of making a strip of this steel
RU2586933C1 (en) * 2015-06-08 2016-06-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Южно-Уральский государственный университет" (национальный исследовательский университет) (ФГБОУ ВПО "ЮУрГУ" (НИУ)) Martensite corrosion-resistant chrome-containing steel with improved machinability
RU2606825C1 (en) * 2015-06-24 2017-01-10 Федеральное Государственное Унитарное Предприятие "Центральный Научно-Исследовательский Институт Конструкционных Материалов "Прометей" (Фгуп "Цнии Км "Прометей") High-strength wear-resistant steel for agricultural machines (versions)
CN105316572A (en) * 2015-11-25 2016-02-10 怀宁县明月矿山开发有限责任公司 Wear-resistant steel plate for mining machinery
DE102016203969A1 (en) * 2016-03-10 2017-09-14 Thyssenkrupp Ag Process for the heat treatment of a flat steel product, heat-treated steel flat product and its use
BR112018070440B1 (en) 2016-04-19 2022-07-19 Jfe Steel Corporation ABRASION RESISTANT STEEL PLATE AND METHOD FOR PRODUCING ABRASION RESISTANT STEEL PLATE
CN106636919A (en) * 2016-12-09 2017-05-10 天长市天龙泵阀成套设备厂 Anti-abrasion alloy steel
RU2660786C1 (en) * 2017-12-19 2018-07-09 Юлия Алексеевна Щепочкина Iron-based alloy
KR102498144B1 (en) * 2020-12-18 2023-02-08 주식회사 포스코 Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof

Family Cites Families (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE426177B (en) * 1979-12-03 1982-12-13 Uddeholms Ab Hot work tool steel
US4348800A (en) * 1980-04-14 1982-09-14 Republic Steel Corporation Production of steel products with medium to high contents of carbon and manganese and superior surface quality
JPS5861219A (en) * 1981-09-28 1983-04-12 Nippon Steel Corp High tensile tough steel with superior delayed rupture resistance
JPH075970B2 (en) * 1989-12-18 1995-01-25 住友金属工業株式会社 High carbon steel sheet manufacturing method
JPH0441616A (en) * 1990-06-06 1992-02-12 Nkk Corp Production of low-hardness water-resistant steel excellent in wear resistance and bendability
US5284529A (en) * 1990-06-06 1994-02-08 Nkk Corporation Abrasion-resistant steel
US5393358A (en) * 1990-12-03 1995-02-28 Nkk Corporation Method for producing abrasion-resistant steel having excellent surface property
JP3273391B2 (en) * 1993-12-16 2002-04-08 新日本製鐵株式会社 Manufacturing method of good workability wear-resistant steel plate
FR2726287B1 (en) * 1994-10-31 1997-01-03 Creusot Loire LOW ALLOY STEEL FOR THE MANUFACTURE OF MOLDS FOR PLASTICS OR FOR RUBBER
FR2729974B1 (en) * 1995-01-31 1997-02-28 Creusot Loire HIGH DUCTILITY STEEL, MANUFACTURING PROCESS AND USE
FR2733516B1 (en) 1995-04-27 1997-05-30 Creusot Loire STEEL AND PROCESS FOR THE MANUFACTURE OF PARTS WITH HIGH ABRASION RESISTANCE
JPH09249935A (en) * 1996-03-13 1997-09-22 Sumitomo Metal Ind Ltd High strength steel material excellent in sulfide stress cracking resistance and its production
GB9608108D0 (en) * 1996-04-19 1996-06-26 Naco Inc Steel Castings
CN1074468C (en) * 1997-01-28 2001-11-07 山东工业大学 Multielement micro-alloyed air cooled bainitic steel
US5865385A (en) * 1997-02-21 1999-02-02 Arnett; Charles R. Comminuting media comprising martensitic/austenitic steel containing retained work-transformable austenite
DE19710125A1 (en) * 1997-03-13 1998-09-17 Krupp Ag Hoesch Krupp Process for the production of a steel strip with high strength and good formability
JP3475706B2 (en) * 1997-03-28 2003-12-08 住友金属工業株式会社 High-strength, high-toughness tempered steel with excellent machinability
TW454040B (en) * 1997-12-19 2001-09-11 Exxon Production Research Co Ultra-high strength ausaged steels with excellent cryogenic temperature toughness
FR2796966B1 (en) * 1999-07-30 2001-09-21 Ugine Sa PROCESS FOR THE MANUFACTURE OF THIN STRIP OF TRIP-TYPE STEEL AND THIN STRIP THUS OBTAINED
JP2003027181A (en) * 2001-07-12 2003-01-29 Komatsu Ltd High-toughness, wear-resistant steel
FR2847272B1 (en) * 2002-11-19 2004-12-24 Usinor METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET

Cited By (38)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101775545B (en) * 2009-01-14 2011-10-12 宝山钢铁股份有限公司 Low-alloy high-strength high-toughness wear-resistant steel plate and manufacturing method thereof
CN102134682B (en) * 2010-01-22 2013-01-02 宝山钢铁股份有限公司 Wear resistant steel plate
CN102199737B (en) * 2010-03-26 2012-09-19 宝山钢铁股份有限公司 600HB-grade wear resistant steel plate and its manufacturing method
CN102199737A (en) * 2010-03-26 2011-09-28 宝山钢铁股份有限公司 600HB-grade wear resistant steel plate and its manufacturing method
US9340233B2 (en) 2010-10-15 2016-05-17 Benteler Automobiltechnik Gmbh Method for producing a hot-formed and press-hardened metal component
CN102453791A (en) * 2010-10-15 2012-05-16 本特勒尔汽车技术有限公司 Automobile column and method for producing a hot-formed and press-hardened automobile column
CN103748288B (en) * 2011-08-20 2016-08-24 卡特彼勒公司 The scraper component of bi-material layers for the elevator system of wheeled self-propelled scraper
CN103748288A (en) * 2011-08-20 2014-04-23 卡特彼勒公司 Bimaterial flight assembly for an elevator system for a wheel tractor scraper
US9689050B2 (en) 2011-09-06 2017-06-27 Arcelormittal Investigación Y Desarrollo S.L. Rolled steel that hardens by means of precipitation after hot-forming and/or quenching with a tool having very high strength and ductility, and method for manufacturing same
CN103958718A (en) * 2011-11-01 2014-07-30 霍尼韦尔国际公司 Low nickel austenitic stainless steel
CN102433505A (en) * 2011-12-14 2012-05-02 虞海盈 Material for producing rolling bearings
CN103205639A (en) * 2013-03-14 2013-07-17 长安大学 Shovel blade cutting edge of loader and method for manufacturing shovel blade cutting edge
CN103320695A (en) * 2013-06-19 2013-09-25 侯宇岷 Large-diameter wear-resistant steel ball and production process thereof
CN105723004A (en) * 2013-08-30 2016-06-29 罗奇钢铁公司 A high-hardness hot-rolled steel product, and a method of manufacturing the same
CN105723004B (en) * 2013-08-30 2018-01-12 罗奇钢铁公司 High-hardness hot rolled steel product and its manufacture method
CN103898299A (en) * 2014-04-04 2014-07-02 北京科技大学 Preparation method for 2400MPa class low-cost nano bainitic steel
CN103898299B (en) * 2014-04-04 2016-04-13 北京科技大学 A kind of preparation method of 2400MPa level low cost nanometer bainitic steel
CN104032216A (en) * 2014-06-27 2014-09-10 张家港市佳威机械有限公司 Composite manganese-steel alloy
CN104152820A (en) * 2014-07-16 2014-11-19 安徽省三方耐磨股份有限公司 Novel alloy lining plate
CN104131224A (en) * 2014-07-25 2014-11-05 合肥市东庐机械制造有限公司 Wear-resistant impact-resistant alloy steel and manufacturing method thereof
CN104213041A (en) * 2014-08-28 2014-12-17 南京赛达机械制造有限公司 Wear-resisting steel for turbine blade and production process t hereof
CN105506481A (en) * 2014-09-29 2016-04-20 铜陵有色金神耐磨材料有限责任公司 Manufacturing method of impact-resistant alloy grinding balls
CN105039864A (en) * 2015-07-13 2015-11-11 江苏曜曜铸业有限公司 Alloy used for spindle box mould
CN105018863A (en) * 2015-07-13 2015-11-04 江苏曜曜铸业有限公司 Alloy used for clutch housing mould
CN105568142A (en) * 2016-03-09 2016-05-11 桂林电子科技大学 High-strength and high-tenacity low-alloy wear-resistant steel excavator bucket tooth and preparing method thereof
CN105568142B (en) * 2016-03-09 2017-07-28 桂林电子科技大学 A kind of high-obdurability low-alloy abrasion-resistant stee excavator bucket teeth and preparation method thereof
CN105886946A (en) * 2016-04-15 2016-08-24 芜湖德业摩擦材料有限公司 Preparing method of brake pad friction block
CN105779891A (en) * 2016-04-15 2016-07-20 芜湖德业摩擦材料有限公司 Preparation method for high-hardness friction block for brake pad
CN106811680A (en) * 2016-12-28 2017-06-09 芜湖市永帆精密模具科技有限公司 A kind of low-alloy impact-resistant abrasion-proof steel ball and preparation method thereof
CN112703263A (en) * 2018-09-12 2021-04-23 杰富意钢铁株式会社 Steel material and method for producing same
CN114729435A (en) * 2019-12-16 2022-07-08 株式会社Posco High-hardness wear-resistant steel with excellent low-temperature impact toughness and manufacturing method thereof
CN111647820B (en) * 2020-06-15 2022-01-11 山东建筑大学 Advanced high-strength steel and segmented preparation method and application thereof
CN111647820A (en) * 2020-06-15 2020-09-11 山东建筑大学 Advanced high-strength steel and segmented preparation method and application thereof
CN111690880A (en) * 2020-08-08 2020-09-22 湖南长重机器股份有限公司 Impact-resistant lining plate of bucket wheel machine hopper
CN111690880B (en) * 2020-08-08 2021-11-19 湖南长重机器股份有限公司 Impact-resistant lining plate of bucket wheel machine hopper
CN112695253A (en) * 2020-12-22 2021-04-23 江西耐普矿机股份有限公司 Carbide-containing high-strength high-toughness bainite wear-resistant steel and preparation method thereof
CN112899571A (en) * 2021-01-19 2021-06-04 山东钢铁股份有限公司 Fatigue-resistant corrosion-resistant round steel for forging and pressing and preparation method thereof
CN113444985A (en) * 2021-05-24 2021-09-28 北京中永业科技有限公司 Steel material and preparation method thereof

Also Published As

Publication number Publication date
AR042071A1 (en) 2005-06-08
UA80308C2 (en) 2007-09-10
KR20050083913A (en) 2005-08-26
US20080247903A1 (en) 2008-10-09
EP1563104B1 (en) 2008-07-09
ZA200504005B (en) 2006-07-26
ES2309377T3 (en) 2008-12-16
CA2506351C (en) 2012-04-24
DE60322092D1 (en) 2008-08-21
BR122013002046B8 (en) 2017-12-19
BR122013002046B1 (en) 2017-04-25
SI1563104T1 (en) 2008-12-31
US20060137780A1 (en) 2006-06-29
CN100350061C (en) 2007-11-21
US20080253920A1 (en) 2008-10-16
PL375544A1 (en) 2005-11-28
ATE400667T1 (en) 2008-07-15
PL204080B1 (en) 2009-12-31
JP4535877B2 (en) 2010-09-01
BR0315697A (en) 2005-09-20
PE20040487A1 (en) 2004-08-18
RU2005119208A (en) 2006-02-10
FR2847270A1 (en) 2004-05-21
US7459041B2 (en) 2008-12-02
KR101010570B1 (en) 2011-01-25
US8709336B2 (en) 2014-04-29
AU2003290188B2 (en) 2009-01-08
CA2506351A1 (en) 2004-06-10
JP2006506528A (en) 2006-02-23
EP1563104A1 (en) 2005-08-17
BR0315697B1 (en) 2013-07-30
WO2004048620A1 (en) 2004-06-10
FR2847270B1 (en) 2004-12-24
RU2327802C2 (en) 2008-06-27
AU2003290188A1 (en) 2004-06-18

Similar Documents

Publication Publication Date Title
CN100350061C (en) Method for making an abrasion resistant steel plate and plate obtained
CN1714161A (en) Method for making an abrasion resistant steel plate and plate obtained
CN1714159A (en) Method for making an abrasion resistant steel plate and plate obtained
CN1186472C (en) High-speed steel roll ring and its production
CN103556083B (en) The high-speed steel of powder metallurgically manufacturing
CN1648276A (en) Alloy tool steel
CN1511969A (en) Alloy tool steel and its producing method and mold using it
CN100343409C (en) Cold work steel and cold work tool
CN1254555C (en) Wearable cast steel in microalloy martensite and manufacturing method
JPH08295990A (en) Preparation of highly wear-resistant steel and steel product
KR100836699B1 (en) Die steel
CN1706976A (en) Multielement high-nickel chromium wear-resistant cast iron and its prepn process
EP1637615B1 (en) Heat-resisting steel, heat treatment method for heat-resisting steel and high-temperature steam turbine rotor
CN1219904C (en) Wearproof and tough quasi bainite points and rails and their production
CN101445892A (en) High boron high-speed steel roll material
CN1166803C (en) High vanadium high-wear-resistant alloy and its preparation method
CN1288270C (en) Cooled and tempered bainite steel part and its mfg. process
JP5522854B2 (en) Cold tool steel and manufacturing method thereof
CN105886918B (en) A kind of multi-element composite micro-alloying casting bucket tooth and preparation method thereof
CN1226441C (en) Reinforced durable tool steel method for the production thereof method for producing parts made of said steel and parts thus obtained
CN108715976B (en) Ti-Zr-C particle reinforced wear-resistant steel and preparation method thereof
CN101258258A (en) Powder metallurgically manufactured high speed steel
CN1844434A (en) Steel for loader shovel tool blade and method for producing same
CN104561813B (en) A kind of middle carbon silicomanganese system high abrasion air cooling steel
JP2000328199A (en) Wear resistant material

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
C14 Grant of patent or utility model
GR01 Patent grant
ASS Succession or assignment of patent right

Owner name: INDUSTEEL FRANCE

Free format text: FORMER OWNER: INDUSTEEL CREUSOT

Effective date: 20150804

C41 Transfer of patent application or patent right or utility model
TR01 Transfer of patent right

Effective date of registration: 20150804

Address after: France Denis

Patentee after: INDUSTEEL FRANCE

Address before: French pitot

Patentee before: Industeel Creusot

CX01 Expiry of patent term

Granted publication date: 20071121

CX01 Expiry of patent term